study on hook formation in ultra-low carbon steel …ccc.illinois.edu/s/2005_presentations/12...2...
TRANSCRIPT
1
ANNUAL REPORT 2005Meeting date: June 1, 2005
Joydeep SenguptaPostdoctoral Research Associate
& Brian G. Thomas
Department of Mechanical & Industrial EngineeringUniversity of Illinois at Urbana-Champaign
Study on Hook Formation in Ultra-low Carbon Steel Slabs
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 2
Scale
10 mm0
Oscillation mark
Location of transverse crack
Pitch of OM
Hook-type OMs are generally deeper and can be distinguished visually
Types of oscillation marks
POSCO casting trials on ultra-low carbon slabs (2004):• Typical OM depth = ~0.2 – 0.6 mm• OMs with hooks > 98% on narrow face for different casting conditions (12 out of 13)
= 100% on wide face (7 out of 10) – 70-90% (3 out of 10)
Szekeres, Iron & SteelMaker, 1996
2
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 3
Types of hook marks (ultra-low carbon steel)
Entrapped inclusion
Curved hook
Straighthook
Scale
1 mm0
• ~20-35% straight hooks (wide + narrow faces) based on 13 POSCO trials in 2004• OMs with curved hooks are generally deeper (~1.5 times) • Scarfing is usually done to remove hooks & related defects
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 4
OM/Hook formation more severe with decreasing carbon content
OMOM
OM
Ultra-low Peritectic Medium
10 mm
200
µ m
Badri et al., Met. Trans. B, 2005Suzuki, CAMP-ISIJ, 1998
• Ultra-low carbon steels have deeper OMs and are more prone to form hooks• Higher solidus (1535 °C ↔ 1500 °C for high carbon steels) &
thinner mushy zone (15 °C ↔ 50 °C for high carbon steels)
3
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 5
OM/Hook formation in meniscus region
• Combined effect of heat transfer, solidification, mechanical interactions & fluid flow• Meniscus region: extends to ~10 mm below the metal level• Influencing events last for a very short time-span but occurs periodically
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 6
Influential event #1
Heat transfer between shell and mold:Heat is conducted into the mold via liquid flux & re-solidified flux layers• Governed by size & properties of interfacial gap (contact resistance)• Dynamic mold distortion can lower contact resistance locally
Li and Thomas, Private Communication, 2005
-5.0E+05
0.0E+00
5.0E+05
1.0E+06
1.5E+06
2.0E+06
2.5E+06
0 1 2 3 4 5 6
Time (s)
Hea
t flu
x (W
/m2 )
5.75 inch on mould6.35 mm on casting5.25 inch mm on mould19.05 mm on casting
0.0mm
6.35mm
12.70mm
19.05mm
Casting
5.25"
5.50"
5.75"
6.00"
6.25"
6.50"Mould
Slab
Mold
Meng and Thomas, Met. Trans. B, 2004
4
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 7
Periodic rise in heat flux near meniscus
Badri et al., Met. Trans. B, 2005
NST NST
Measurements for ulta-low carbon steel in a laboratory scale simulator at CMU
Rise in heat flux attributed to release of latent heat (meniscus freezing)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 8
Link between periodic rise in heat transfer & OM formation
Badri et al., Met. Trans. B, 2005
Measurements for ulta-low carbon steel in a laboratory scale simulator at CMU
Oscillation marks on a ultra-low carbon steel slab
Periodic rise in heat flux during NST
5
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 9
Influential event #2
Meniscus shape:• Shape determined by balance of surface tension, pressure & gravity forces
(equilibrium shape can be predicted by Bikerman’s equation)
• Strong function of sulfur content of steel
• Pressure forces due to mold oscillation is transmitted to meniscus via flux layer(both temporal & spatial variations)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 10
Equilibrium meniscus shape
zza22aln
2aza2xx
2222
0−+
+−−=−
)12ln(2
aax0 +−=
g2asteelρ
γ=
x = distance perpendicular to the mold wall in mmZ = distance along the mold wall in mmγ = surface tension between liquid steel and vapor (or flux) in N m-1
ρsteel = density of liquid steel = 7000 kg m-3
g = gravitational acceleration = 9.81 m s-2
From Bikerman, Physical Surfaces, Academic Press, 1970
γ
z
x
Liquid flux
Liquid steel
ρsteel
6
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 11
Effect of %S on surface tension
Lee and Morita, ISIJ International, 2002
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 12
Meniscus shape – affected by sulfur content
-8
-7
-6
-5
-4
-3
-2
-1
00 5 10 15 20 25 30 35
Horizontal distance, x (mm)
Ver
tical
dis
tanc
e, z
(mm
)
Fe-0.001 pct SFe-0.01 pct SFe-0.1 pct S
γ = ~1.8 N m-1
γ = ~1.6 N m-1
γ = ~1.3 N m-1
Temperature = 1550 oCDensity of liquid steel = 7000 kg m-3
z
x
Liquid flux
Liquid steel
7
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 13
Dynamic flow effects at meniscus(due to mold oscillation)
Meniscus is at a sharp angle
to shell tip
Time (s)
Mol
d di
spla
cem
ent (
mm
)
Meniscus shape is flat and angular
Meniscus is smoothly curved
Meniscus is elevated and bulged out
Negative strip
Increasing positive flux pressure:• Brings meniscus close to mold
• Facilitates sudden freezing
Increasing negative flux pressure: • Pushes meniscus away from mold
• Meniscus Bulging
Increasing positive flux pressure:• Brings meniscus close to mold
• Facilitates sudden freezing
Increasing negative flux pressure: • Pushes meniscus away from mold
• Meniscus Bulging
Tanaka and Takatani, CAMP-ISIJ, 1989
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 14
Influential event #3
Meniscus Freezing:Partial solidification of meniscus can occur in presence of a water-cooled mold (Saucedo, 1991)
• Preservation of instanteneous frozen shape
• Rapid cell growth in the presence of under-cooled liquid (heterogeneous nucleation)
• Incorporated into OM mechanisms(Takeuchi & Brimacombe in 1984)
Yamamura et al., ISIJ International, 1996
8
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 15
Influential event #4
Fluid flow effects:• Steel jets perturb free surface (standing waves)
• Level fluctuations due to chaotic turbulence & presence of particles/bubbles(buoyancy forces)
• Abrupt changes in operating conditions (e.g. release of nozzle clog)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 16
Local level fluctuations
Lai et al., ISS Steelmaking Conference, 2000
9
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 17
Influential event #5
Delivery of local superheat:• Distributed via metal jets & follows the fluid flow patterns to reach meniscus• Meniscus typically retains ~30% of total superheat available (no freezing)
0 20 40 60 80 1000
50
100
150
200
250
Casting width: 1300 mmCenter of narrow face
Sup
erhe
at fl
ux (M
W/m
2 )
Distance below meniscus (mm)
Casting speed: 1.2 m/min Casting speed: 1.46 m/min Casting speed: 1.7 m/min
Zhang and Thomas, POSCO Report, 2004
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 18
Influential event #6
Shell tip deformation:Shell tip may move away or towards the mold surface due to thermal stresses(temperature gradients) and/or mechanical effects
• Solidification mode (large shrinkage is associated with δ→γ transformation)
• Local shell thinning due to presence of air gap & OMs (coupled effect)
• Mechanical interaction between shell tip and solid rim (negative strip period)
• Sticking of shell tip to mold wall in absence of flux (hot tearing)
• Sudden level fluctuation exposing shell interior to flux
10
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 19
Level drop effect: shell bending
B.G. Thomas and H. Zhu, Solidification Science & Processing Conference, 1996
• During level drop:Shell interior exposed to fluxLeft edge of shell cools rapidlyShell tip bends away from mold
• After level rise:New shell forms on existing solidBending of shell increased further
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 20
OM formation mechanism I
Healing: (i) Sato (Proc. of NOH & BOS Conf.), 1979(ii) Szekeres (Iron & Steel Engineer), 1996
Tearing: Savage and Pritchard (Iron and Steel), 1954
Steel solidifies first against mold wall forming a secondary meniscus& attaches to shell during negative strip time
11
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 21
OM formation mechanism II
Shell bending during negative strip
Liquid steel overflow during positive strip
HookOM
Shell distortion (away from mold) & subsequent overflow
(i) Schwerdtfeger and Sha (Met. Trans. B), 2000: Beam bending theory(ii) Thomas and Zhu, 1996: Level drop causes surface depressions(iii)Emi et al. (Proc. of NOH & BOS Conf.), 1978: Solid flux rim effect
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 22
OM formation mechanism III
Meniscus freezing during negative strip
Liquid steel overflow during positive strip
HookOM
Meniscus freezing & subsequent overflow
(i) Takeuchi and Brimacombe (Met. Trans. B), 1984: Metallography(ii) Saucedo (SteelMaking Conf. Proc.), 1991: Metallography(iii)Putz et al. (Steel Research), 2003: Heat transfer/Fluid flow model
12
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 23
I. Solidification of curved liquid steel meniscus
II. Solidification of steel shell against the mold wall and thensubsequent distortion due to thermal stress / pressure forces
Re-evaluate mechanisms by:• Analysis of hook metallography (POSCO/Postech)• EBSD analysis of hooks• Meniscus shape calculation
• Thermal-stress analysis of initial solidification
Propose new mechanism of hook formation
Two mechanisms for hook formation have been considered in this study
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 24
Hook characteristics
Hook depth, D = 1.82 mmHook height, H = 5.37 mmHook length, L = 5.65 mmHook thickness, T = 0.78 mmOM depth, d = 0.228 mmFinal hook angle, θ = 69o
Ultra low carbon steel (0.003% C)POSCO Sample No.: B58077-02-2 No.1-1 (Curved hook)
1 mm
Scale
0
Outline of hook “rapid solidification” region
θ
L H
d
Hook shape (line of hook origin)
Mold surface
Casting direction
D
T
“Meniscus overflow” region
1 mm
Scale
0
Outline of hook “rapid solidification” region
θ
L H
d
Hook shape (line of hook origin)
Mold surface
Casting direction
D
T
“Meniscus overflow” region
13
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 25
Hook shapes: Case I
Ultra low carbon steel:0.003C-0.009S-0.08Mn-0.013P-0.039Al-0.047Ti-0.01Ni-0.01Cr-0.01Cu
Casting conditions:Casting speed : 1.42 m/minFrequency: 155 cpmStroke: 6.34 mmSuperheat: 25 oC
POSCO Casting No.: B58077-02Samples taken within ~100mm of slab length
0
0.5
1
1.5
2
2.5
3
3.5
4
4.5
5
5.5
6
0 0.5 1 1.5 2 2.5x (mm)
z (m
m)
Actual shapeBikerman curve
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 26
0
0.5
1
1.5
2
2.5
3
3.5
4
4.5
5
5.5
6
0 0.5 1 1.5 2 2.5
Hook shapes: Case II
Ultra low carbon steel:0.003C-0.009S-0.08Mn-0.013P-0.039Al-0.047Ti-0.01Ni-0.01Cr-0.01Cu
Casting conditions:Casting speed : 1.61 m/minFrequency: 181 cpmStroke: 6.82 mmSuperheat: 27 oC
POSCO Casting No.: B58075-06Samples taken within ~100mm of slab length
z (m
m)
Actual shapeBikerman curve
x (mm)
14
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 27
Variations in hook angle, and meniscus shape before & after “meniscus overflow”
Different shapes of meniscus: (a) almost straight to (c) very bentDifferent shapes of overflow region: (a) shallow contact angle, (b) near-vertical contact angle, & (c) strange angle and shape
(a) (b) (c)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 28
A
B
Bubble A entrapped by frozen meniscus butBubble B flows along with the overflowing liquid steel
Debris trapped on both sides of the line of hook origin:
Below the line of hook origin: particles flow up with the steel, reach the meniscus, but do not get entrained into slag layer
Above the line of hook origin: particles flow along with the overflowing liquid steel when it overflows the meniscus
Hooks with particles showing capture before and after “meniscus overflow”
15
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 29
Features of a hook tip
Fractured hook tip
Brittle fracture
Actual position of hook and fractured
tip on slab
Original position of fractured tip prior to
brittle fracture
Location of brittle fracture
Location of melting after
fracture
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 30
Truncated hooks
Fractured hook tip
Truncated hook
Truncated hook and unmelted fractured tip
Truncated hook (Fractured tip melted away)
16
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 31
• Random orientation of dendrites → Heterogeneous nucleation• Fine dendrite arms near origin line → rapid solidification of undercooled liquid• Coarser dendrite arms → Lower temperature gradient
→ long time surrounded by liquid before solidification continued (ripening)• Large sudden change of growth direction → Movement of fractured hook tip
Cell growth near hook
Solidification inward from frozen meniscus
Solidification within the liquid overflow region towards the mold wall
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 32
SEM Images
1 mm
100 µmMicrographfrom optical microscope Backscattered SEM image Backscattered SEM image with
70 degrees tilt
200 µm
Hook shape transferred(to scale)
17
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 33
Electron Back Scattered Diffraction (EBSD) Map near hook region
100 µm
Grains can be identified on the sample by superimposing an EBSD map containing grain orientation information on the Backscattered SEM image
Backscattered SEM image
200 µm
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 34
Quantification of grain misorientation
100 µm 300x
EBSD postprocessor software can provide local grain misorientation data
OVERFLOW REGION
+20o
0o
-1o
+21o+50o
+34o
18
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 35
Location of line of hook origin on EBSD image compares well with micrograph
200 µm
OVERFLOW REGION
LINE OF HOOK
ORIGIN
FROZEN MENISCUS
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 36
v
xz
y
Solidifyingsteel shell
Position of meniscusz = v x t
CON2D Finite-element model to compute thermal distortion of solidifying steel shell
Simulation Details • Domain Size: 3 mm x 30 mm• 6 noded triangular elements• Mesh resolution: 0.1 mm x 0.5 mm
Assumptions:• Effect of ferrostatic pressure is ignored• No constraint at the mold edge• No mold taper, slag, oscillation, friction• Drop in heat transfer due to air gap ignored• Level is assumed to drop suddenly• No kinetics & undercooling effects
19
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 37
Simulation conditions
1.5 s (0.001 s time step size)1.2 s0.8 s (for 16, 8, 5 & 3 mm)1000 °C250 °C1.2 m/min30 °C14.6 °C1533.9 °C1519.3 °C
0.003C-0.009S-0.08Mn-0.013P-0.039Al-0.047Ti-0.01Ni-0.01Cr-0.01Cu
Ultra-low C steel
Sudden level rise atSudden level drop at
Total time for analysis
Tflux
Tmold
Casting speed∆Tsuperheat
∆TTliquidus
Tsolidus
CompositionGrade
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 38
Phase fractions
0
0.2
0.4
0.6
0.8
1
1.2
1350 1370 1390 1410 1430 1450 1470 1490 1510 1530 1550
Temperature ( oC)
Phas
e fr
actio
n
delta-ferriteausteniteliquid
Mushy zone
20
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 39
Thermophysical properties
25
30
35
40
45
50
750 850 950 1050 1150 1250 1350 1450 1550
Temperature ( oC)
The
rmal
Con
duct
ivity
(W m
-1 K
-1)
0.25
0.5
0.75
1
1.25
1.5
Ent
halp
y (M
J kg
-1)
Thermal conductivityEnthalpy
Tliquidus
Thermal conductivity at T > Tliquidus = 259. 35 Wm-1 (~6.65x)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 40
Mechanical properties
0
10
20
30
40
50
60
70
80
90
100
750 850 950 1050 1150 1250 1350 1450 1550
Temperature ( oC)
You
ng's
Mod
ulus
(GPa
)
-0.02
-0.016
-0.012
-0.008
-0.004
0
0.004
0.008
0.012
0.016
0.02
The
rmal
Lin
ear
Exp
ansi
on (-
)
Young's ModulusThermal linear expansion coefficient
Young's modulus at T > Tliquidus = 100 MPaTliquidus
21
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 41
Constitutive behavior
Plastic Strain (%)
Stre
ss(M
Pa)
0 2 4 6 80
5
10
15
20
25 Strain Rate = 1x10-4 1/sec.
Symbols: Experiments [YM WON, Met. Trans. B, 2000]Lines: CON2D (Koslowski III)
1100 oC
1200 oC
1300 oC
Plastic Strain (%)
Stre
ss(M
Pa)
0 2 4 6 80
1
2
3
CON2D, 1425 oCCON2D, 1525 oCExperiment, 1425 oCExperiment, 1525 oC
Strain Rate = 1.4x10-4
Kozlowski III Law for Austenite Power Law for δ-ferrite
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 42
Heat Transfer Calculations
Qmold
0
5
10
15
20
25
30
0 0.25 0.5 0.75 1 1.25 1.5
Time (s)
Men
iscu
s lev
el (m
m)
A
B
C
Mold - solidifying shell interface:Qmold = hmold x (Tshell – 250)hmold = 4000 Wm2K-1
Slag – shell interface:Qslag = hslag x (Tshell – Tslag)hslag = 2300 Wm2K-1
Tslag = 1000 oC
Level fluctuation history
Qslag
Qmold
Qmold
Liquid steel
Liquid steel
Liquid steel
Shell Shell Shell
ComputationalDomain
3 x 30 mm
A: Before Level Drop B: During Level Drop C: After Level Rise
Meniscus
Meniscus
Meniscus
Liquid flux
@ 1000 oC
22
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 43
Shell deformation during level fluctuation
0
5
10
15
20
25
30
0.7 s 1.1 s
Level drop0.8 s
Level rise1.2 s
Time1.5 s
t = 0.7sNormal solidification & shell growth
t = 1.1sShell cools without growth & bends
t = 1.5sShell grows again with further bending
15001450140013501300125012001150110010501000950900850800750700650600550500
Tem
pera
ture
°C
-30
-25
-20
-15
-10
-5
0
5
10
0 0.5 1 1.5
Time (s)
Men
iscu
s lev
el (m
m)
-10
-5
0
5
10
15
20
25
30
35
0 0.5 1 1.5
Time (s)
Met
al le
vel w
.r.t.
shel
l (m
m)
Leve
l dro
p =
16 m
m
Leve
l ris
e =
24 m
m
Cas
ting
spee
d =
20 m
m/s
∆u = +0.35 mm
∆u = +0.05 mm
Level
Level
Level
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 44
Final distorted shape for different level drop distances (0.3s after overflow over shell tip)
Z(m
m)
0 2 40
5
10
15
20
25
30
0 2 40
5
10
15
20
25
30
0 2 40
5
10
15
20
25
30
0 2 40
5
10
15
20
25
30
0 2 40
5
10
15
20
25
3015001450140013501300125012001150110010501000950900850800750700650600550500
No Level Drop∆u = +0.02 mm
3mm drop∆u = +0.02 mm
5mm drop∆u = +0.05 mm
8mm drop∆u = +0.175 mm
16mm drop∆u = +0.35 mm
Temperature °C
Level Drop
Level Drop
Level Drop
Level Drop
LD time: 0.4s
23
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 45
Jog
Fredriksson and Elfsberg, Scandinavian J. of Met., 2002
Shell
Jog formation
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 46
Comparison between hook and distorted shell shapes
MeniscusOverflow
Deformed shell after level rise
Mold surface
∆u = +0.35 mm
Hook
x (mm)
z (m
m)
1 2
1
2
3
4
5
6Predicted for 16 mm level drop
Predicted for 8 mm level drop
Measured hook shape
Mechanism of hook formation due to shell distortion associated with a
level drop event Shell distortion will affect OM & hook formation during large level drops
POSCO Casting No.: B58077-02
24
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 47
Hook depth measured from POSCO samples (2004 data)
0.532.611.6056.044.028225051B30959-55
0.553.211.7961.538.532205151B30959-51
0.421.911.0560.439.629194848B30959-02
0.533.211.1267.332.735175355B30957-01
0.521.581.0365.434.61792626B26848-54
0.622.051.0988.911.12432727B26848-04
0.212.100.9677.122.937114848B31077-54
0.471.921.0682.417.64295152B31077-04
0.381.831.1170.229.833144748B31075-05
0.341.490.7756.843.225194451B31075-04
0.291.600.7375.424.646156162B32793-52
0.441.300.8380.919.13894749B32793-05
0.391.530.8377.122.937114849B32793-02
Min hook depth (mm)
Max hook depth (mm)
Mean hook depth (mm)
% Curved hooks
% Surface hooks
Curved hook #
Surface hook #
Hook #
OM #Sample
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 48
Proposed mechanism for hook formation
HOOK FORMATION
CURVED HOOK
STRAIGHT HOOK
Mechanism:Meniscus freezing &
Liquid overflow in the presence of uncooled liquid during negative strip time
Mechanism:Shell distortion during
negative strip time
25
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 49
Development of a detailed hook formation mechanism
• Events dictating formation of OMs and hooks are complex, inter-dependent and transient
• Plant experiments cannot reveal detailed steps that lead to final microstructure and morphology
• Development of a comprehensive computational model is a daunting task
• Alternative methodology:- Combine existing modeling results & plant observations- Construct a series of schematics illustrating the mechanism- Will not predict formation of hooks, but will lead to model development
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 50
Three hooks observed on a POSCO slab
8 m
m8
mm
Hook #3
Hook #2
Hook #1
I. Steel Composition: C (0.003%) - Mn (0.08%) - Si (0.005%) - P (0.015%) – S (0.01%) - Cr (0.01%) - Ni (0.01%) - Cu (0.01%) – Ti (0.05%) - Al (0.04%) II. Steel Properties: Liquidus temperature (in °C): 1533 Solidus temperature (in °C): 1517 Density of liquid steel (in kg m-3): 7000 Surface tension at 1550 °C (in N m-1): 1.6 III. Slag Properties: Solidification temperature (in °C): 1149 Melting temperature (in °C): 1180 Viscosity at 1300 °C (in Poise): 3.21 IV. Casting conditions: Casting speed: 1.394 m min-1
Frequency of mold oscillation: 174 cpm Stroke of mold oscillation: 5.89 mm Theoretical pitch for oscillation marks (speed/frequency):
8.01 mm
Superheat: 32 °C
26
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 51
Objectives
I. Graphically track the positions of the following on a Cartesian space for one mold oscillation cycle:Meniscus, mold, solid/liquid flux interface, shell, OM/Hook mark nos. 2 & 3
II. Using above positions and final morphology of the cast slab sample as templates, events leading to formation of OM & hook mark no. 1 will be identified
Solid flux rim
Liquid flux
channel
Shell
Liquid steel
Meniscus
Cartesian space under scrutiny
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 52
Equilibrium shape of meniscus
-8
-7
-6
-5
-4
-3
-2
-1
00 5 10 15 20 25 30 35
Horizontal distance, x (mm)
Ver
tical
dis
tanc
e, z
(mm
)
Fe-0.001 pct STemperature = 1550 oCDensity of liquid steel = 7000 kg m-3
Assumptions: I. Far field metal level remains unpeturbed at all times (z = 0 mm) II. x = 0 mm corresponds to mold wallIII. Dynamic effects active for x < 35 mm
Extends to far-field metal level(towards SEN)
MENISCUS REGION
SHELL
LIQUID STEEL
27
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 53
Mold & shell velocity
-90-80-70-60-50-40-30-20-10
0102030405060708090
0 0.05 0.1 0.15 0.2 0.25 0.3 0.35
Time (s)
Vel
ocity
(mm
/s)
Shell
Oscillating mold
NEGATIVE STRIP
(a)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 54
Mold position
-24-22-20-18-16-14-12-10-8-6-4-20246
0 0.05 0.1 0.15 0.2 0.25 0.3 0.35
Time (s)
z (m
m)
Mold position w.r.t meniscus level
OM#2 position w.r.t. meniscus level
Meniscus levelz = 0 mm
LABORATORY FRAME
Casting speed = 23.23 mm/s (1.394 m/min)Stroke = 5.89 mmFrequency = 2.90 cps (174 cpm)
NEGATIVE STRIP
(b)
Meniscus shape is assumed to be in equilibrium at tstart = 0 s• Mold acceleration is zero → Inertia force is absent at this instant• Positive flux pressure built-up during NST has been dissipated completely• Hence, only surface tension forces will determine the shape of meniscus
At tstart = 0 s:Position of OM #2:6.4 + 8 = 12.4 mm
Position of OM #3:12.4 + 8 = 20.4 mm
Position corresponds to z = 0 mm & lines up with far-field metal level
28
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 55
Profile of solid flux rim
Takeuchi et al., 1983
• Profile of solid rim above the meniscus has been reported in literature, with: Solidus for steel = 1399 oC (actual 1517 oC)Solidus for slag = 1130 oC(actual 1180 oC)Superheat = 5 oC
• The shape has to be modified to correspond to actual superheat of 20 oC
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 56
Evolution of shell thickness predicted by CON1D
0
0.5
1
1.5
2
2.5
3
0 10 20 30 40 50Distance (z) from meniscus level (mm)
Loc
atio
n (x
) pre
dict
ed b
y C
ON
1D (m
m)
LiquidusSolidusShell position
Note: Fraction solid used by CON1D for shell location = 0.5
Cast surface
OM#2
OM#3
OM#1
29
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 57
Reduction in shell thickness due to OM
From B.G. Thomas et al., Sensors & Modeling in Mat. Processing, 1997
OM area for OM nos. 1, 2 & 3:(0.2 + 0.16 + 0.24)/0.236 = 2.54 mm2/cm at ~20 mm below meniscus
Based on literature, about ~16% reduction in shell thickness should be observed at each oscillation mark.(Actual for OM#3 = 17%)
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 58
Summary of events in one oscillation cycle
-6
-4
-2
0
2
4
0 0.05 0.1 0.15 0.2 0.25 0.3 0.35
Time (s)
Mol
d po
sitio
n (m
m)
NEGATIVE STRIP
1. Mold moves upwards2. Flux channel above meniscus opens up3. Liquid flux is sucked into this gap4. Suction rate decreases as mold goes to maxima5. Meniscus shape bulges up & away from mold
1. Mold moves downwards2. Flux channel closes up gradually3. Liquid flux is pumped out of above4. But it is also pumped into the flux channel along mold edge5. Meniscus shape flattens out6. Heat flow into mold increases
Freezing of meniscus
Meniscus overflow begins
Rapid growth of new hook
Growth of new hook completed
Brittle fracture of hook tip
1. Mold moves upwards again2. Flux channel opens up again 3. Intake of liquid flux is increased4. Meniscus is pulled towards its equilibrium shape
Meniscus has equilibrium shape
Equilibrium shape of meniscus is restored as a new cycle of mold oscillation begins
New shell begins to grow above hook & OM is formed
95
49
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 59
Experimental observations on a Sn-Pballoy/stearic acid based casting simulator
Sudden decrease in ys during NST caused by liquid steel overflow over a
hook & subsequent solidification
Sudden rise in tracer velocity during PST caused by creation of additional space in tracer channel due to OM
formation
Tsutsumi et al., ISIJ International, 2000
96
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 60
Summary
I. A new mechanism of hook formation proposed based on:- Analysis of hook micrographs & EBSD images- Meniscus shape predictions by Bikerman equation- Prediction of distorted shell shapes by modifying CON2D- Comparison of hook shapes with both meniscus shapes and
distorted shell shapes(Most hooks match best with meniscus shape)
97
50
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 61
Summary
II. Hook formation has been graphically animated & depicts:- Change of meniscus shape during one oscillation cycle- Menicus freezing during negative strip period- Overflow of liquid steel over curved hook (frozen meniscus)
during negative strip period- Hook formation & growth and subsequent fracture of tip
III. The new mechanism can satisfactorily explain the formation of oscillation marks and hooks in ultra-low carbon steel slabsHowever, shell distortion can still play an important role during oscillation mark formation in pertectic steels.
98
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 62
Shell distortions for different grades without any level fluctuation
X(mm)
Leng
thof
Shel
l(m
m)
0 2 40
2
4
6
8
10
12
14
16
18
20
22
24
26
28
3015101500149014801470146014501440143014201410140013901380137013601350
X(mm)
Leng
thof
Shel
l(m
m)
0 2 40
2
4
6
8
10
12
14
16
18
20
22
24
26
28
30149014801470146014501440143014201410140013901380137013601350
X(mm)
Leng
thof
Shel
l(m
m)
0 2 40
2
4
6
8
10
12
14
16
18
20
22
24
26
28
301440143014201410140013901380137013601350
Fe-0.04% C∆u = 0.04 mm
Fe-0.13% C∆u = 0.42 mm
Fe-0.47% C∆u = 0.02 mm
X(mm)
Leng
thof
Shel
l(m
m)
0 2 40
2
4
6
8
10
12
14
16
18
20
22
24
26
28
301530152015101500149014801470146014501440143014201410140013901380137013601350
Fe-0.003% C∆u = 0.09 mm
99
51
University of Illinois at Urbana-Champaign • Metals Processing Simulation Lab • J. Sengupta 63
Acknowledgements
Continuous Casting ConsortiumUniversity of Illinois
Ho-Jung Shin & Go-Gi LeeGraduate Students, POSTECH, South Korea
For hook samples and micrographs
POSCO, South KoreaFor providing samples and data
Natural Sciences & Engineering Research CouncilCanada
100